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Rational Design of Porous N‑Ti3C2 MXene@CNT Microspheres for High Cycling Stability in Li–S Battery

Jianli Wang1, Zhao Zhang1, Xufeng Yan1, Shunlong Zhang1, Zihao Wu1, Zhihong Zhuang1, Wei‑Qiang Han1 *

* Wei‑Qiang Han, hanwq@zju.edu.cn1 School of Materials Science and Engineering, Zhejiang University, 38 Zheda Road, Hangzhou 310027,

People’s Republic of China

HIGHLIGHTS

• N‑Ti3C2@CNT microspheres are successfully synthesized by the simple spray drying and one‑step pyrolysis.

• Within the microsphere, MXene nanosheets intimately interact with CNTs constructing porous and highly conductive network, which can provide strong immobilization for polysulfides.

• N‑Ti3C2@CNT microsphere/S cathode shows highly cycling stability in lithium‑sulfur battery.

ABSTRACT Herein, N‑Ti3C2@CNT microspheres are suc‑cessfully synthesized by the simple spray drying method. In the preparation process, HCl‑treated melamine (HTM) is selected as the sources of carbon and nitrogen. It not only realizes in situ growth of CNTs on the surface of MXene nanosheets with the catalysis of Ni, but also introduces efficient N‑doping in both MXene and CNTs. Within the microsphere, MXene nanosheets interconnect with CNTs to form porous and conductive network. In addition, N‑doped MXene and CNTs can provide strong chemical immobili‑zation for polysulfides and effectively entrap them within the porous microspheres. Above‑mentioned merits enable N‑Ti3C2@CNT microspheres to be ideal sulfur host. When used in lithium–sulfur (Li–S) battery, the N‑Ti3C2@CNT microspheres/S cathode delivers initial specific capac‑ity of 927 mAh g−1 at 1 C and retains high capacity of 775 mAh g−1 after 1000 cycles with extremely low fading rate (FR) of 0.016% per cycle. Furthermore, the cathode still shows high cycling stability at high C‑rate of 4 C (capacity of 647 mAh g−1 after 650 cycles, FR 0.027%) and high sulfur loading of 3 and 6 mg cm−2 for Li–S batteries.

KEYWORDS Spray drying method; N‑Ti3C2 MXene@CNT microspheres; Nitrogen‑doping; High cycling stability; Lithium–sulfur battery

ISSN 2311‑6706e‑ISSN 2150‑5551

CN 31‑2103/TB

ARTICLE

Cite asNano‑Micro Lett. (2020) 12:4

Received: 25 September 2019 Accepted: 17 November 2019 © The Author(s) 2019

https://doi.org/10.1007/s40820‑019‑0341‑6

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1 Introduction

Lithium–sulfur (Li–S) battery is considered as one of the most promising next‑generation second batteries due to higher energy density (2600 Wh kg−1) and theoretical capac‑ity (1672 mAh g−1) compared with conventional lithium ion batteries. And sulfur is environmentally benign and naturally abundant [1, 2]. However, the practical development of Li–S battery still faces some obstacles. Firstly, sulfur is inherently insulating, which causes inferior capacity performance and poor rate capability. In addition, huge volume change (up to 80%) results in the destruction of cathode structure during cycles. Furthermore, the shuttle effect originated from the dissolution of lithium polysulfides (LiPSs) in electrolytes leads to rapid capacity fading and poor cycle life [3, 4]. To overcome above problems, extensive efforts have been per‑formed including the employment of sulfur host materials [5], the functionalization of separators [6], and the intro‑duction of solid‑state electrolytes [7]. Among these strate‑gies, employing host materials is simple and effective one to promote cathode performance. And lots of researches focused on exploring new materials as ideal sulfur host, which should preferably possess porous structure, excellent electronic conductivity, and strong immobilization for LiPSs [8, 9].

Carbon‑based materials (porous carbon, carbon nano‑tubes, graphene oxide, etc.) were widely applied as sulfur hosts because of good conductivity and abundant porosity [10]. Unfortunately, the physical adsorption for LiPSs is too weak to effectively suppress shuttle effect, indicating unsat‑isfied cycling stability. More studies paid attention to polar metal oxides and metal sulfides, which provide stronger chemical anchoring for LiPSs [11, 12]. However, these mate‑rials (like MnO2, TiO2) usually suffer from intrinsically poor conductivity, which causes sluggish electrochemical kinetics and finally leads to unsatisfied capacity performance and rate capability.

Nazar et al. [13] firstly employed exfoliated MXene as sul‑fur host. It was found that MXene can provide strongly chemi‑cal immobilization for LiPSs via Lewis acid–base affinity. MXene is a large series consisted of ternary metal carbides/nitrides and denoted by Mn+1XnTx, where M is a transition metal such as Ti or Mo, X is carbon and/or nitrogen, and T are surface functional groups such as –OH and –F. Since Gogotsi et al. [14] firstly reported MXene in 2011, various

MXenes have been identified. MXenes have been widely inves‑tigated as the electrode materials due to excellent conductivity, high specific surface area, and good flexibility [15, 16].

MXene is considered as a promising sulfur host in Li–S battery owing to above‑mentioned advantages. However, MXene nanosheets tend to restack on account of hydrogen bonds, which lowers active area and hinders full utilization in Li–S battery [17]. Incorporating another material with MXene to fabricate composite is an effective strategy to solve above problems [18]. In recent years, the composites of MXene/TiO2 [19], MXene/reduce graphene oxide (rGO) [20, 21], MXene/MoS2 [22], and MXene/carbon nanotubes (CNTs) [23, 24] have been reported and showed promoted electrochemical performance compared with single MXene. Nazar et al. [25] prepared interwoven MXene/CNT com‑posites as an effective sulfur host. The additive of CNTs not only prevented aggregation of MXene, but also further improved conductivity of composite. The Lewis acidic affin‑ity and thiosulfate/polythionate conversion jointly formed the dual immobilization for LiPSs, resulting in high cycling stability [26]. However, the direct mixing of MXene and CNTs faces the dispersion problem, and the interaction is inferior. Cheng et al. [27] successfully prepared MXene@CNT composites through CVD strategy, in which CNTs uni‑formly dispersed on the surface of MXene sheets. However, CVD method is involved in harsh conditions. Zhang et al. [28] synthesized Co‑CNT/MXene composites originating from ZIF‑67/MXene for the oxidation–reduction reaction (ORR). Fast electron transfer could be attributed to strong contact between MXene and CNTs via in situ growth of CNTs. But the preparation of ZIF is complicated and hard to control. In addition, the MXene/CNT composites with sphere‑like structure are still not reported.

Herein, we synthesized N‑Ti3C2@CNT composites via a facile method. In the preparation process, HCl‑treated melamine (HTM) was decomposed to realize in situ growth of CNTs on MXene nanosheets at high temperature and introduce nitrogen‑doping. Furtherly, N‑Ti3C2@CNT microspheres were successfully prepared through the spray drying, followed by one‑step pyrolysis. Within the micro‑sphere, N‑Ti3C2 MXene interacted with N‑CNTs to form a 3D well‑interconnected porous network, which facilitated fast electron/ion transfer in electrodes. Nitrogen‑doping could not only improve electronic conductivity, but also promote anchoring capability for LiPSs. As the sulfur host

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in Li–S battery, N‑Ti3C2@CNT microspheres/S cathode demonstrated high specific capacity of 1339.2 mAh g−1 at 0.1 C, excellent rate capability, and superior long cycling stability (capacity decay rate of only 0.016% per cycle after 1000 cycles at 1 C). Good performance was derived from the virtues of microspheres: (1) high specific surface area and abundant porosity provided space to accommodate active sulfur and offered more adsorption sites to anchor LiPSs; (2) efficient incorporation of MXene and CNTs facilitated electron transport across the microspheres, which enhanced electrochemical reaction kinetics; (3) highly polar MXene and N‑doping effectively anchored LiPSs within the micro‑spheres, resulting in highly stable cycling performance. The strategy can also be extended to prepare other CNT micro‑sphere composites and shows great potential in the field of energy storage.

2 Experimental Section

2.1 Preparation of  Ti3C2 MXene Nanosheets

Firstly, Ti3AlC2 (Forsman Technology (Beijing) Co., Ltd) powders were dispersed in hydrofluoric acid (HF, 40 wt%) solution and vigorously stirred for 48 h at room temperature. The suspension was centrifuged and washed in deionized (DI) water for several times. After vacuum dried at 60 °C, multilayered Ti3C2 MXene was obtained. To prepare MXene nanosheets, 1.2 g above‑obtained Ti3C2 MXene was poured into 20 mL tetrabutylammonium hydroxide (TMAOH, 25 wt%) and stirred at room temperature for 24 h. After cen‑trifugation and washing with DI water, the precipitates were dispersed in 200 mL DI water and sonicated for 2 h under Ar atmosphere. The suspension was centrifuged for 1 h at 3500 rpm. The dark green supernatant was collected and stored at 4 °C, which consisted of Ti3C2 MXene nanosheets.

2.2 Preparation of N‑Ti3C2, N‑Ti3C2@CNTs, and N‑Ti3C2@CNT Microspheres

NiCl2 and HCl‑treated melamine were mixed in a certain amount of Ti3C2 nanosheets solution to obtain suspension A. The precipitates were collected by centrifugation and then freeze‑dried for 12 h. The powders were placed in the alu‑mina boat and pyrolyzed at 800 °C for 2 h with the heating

rate of 2 °C min−1 under Ar condition. The as‑received product was designated as N‑Ti3C2@CNTs. As compari‑son, N‑Ti3C2 was prepared by the similar process but from absence of NiCl2. Furtherly, the composite precursors were prepared through the spray drying from suspension A. The powders were heated to 800 °C for 2 h under Ar condition to finally receive N‑Ti3C2@CNT microspheres.

2.3 Preparation of Sulfur Composite Materials

The sulfur composite materials were obtained via the melt‑ing diffusion strategy. Generally, the host material and sul‑fur were mixed with the weight ratio of 3:7 and placed in Teflon‑lined stainless steel autoclave. After 155 °C for 12 h, the sulfur composite materials can be received.

2.4 Materials Characterization

Scanning electron microscopy (SEM, Hitachi SU‑8010) and transmission electron microscopy (TEM, JEM‑2100) measurements were taken to estimate the morphology and internal structure of samples. X‑ray diffraction (XRD) pat‑terns were obtained by Rigaku MiniFlex 600 (Cu Kα radia‑tion). Thermogravimetric analysis (TGA) was performed by the simultaneous thermal analysis instrument (METTLER TOLEDO TGA/DSC 3+). Micromeritics ASAP 2020 Plus HD88 was employed to measure N2 adsorption–desorption curves. The surface chemistry was analyzed based on X‑ray photoelectron spectroscopy (XPS) in Thermo Fisher Scien‑tific Escalab 250Xi.

2.5 Electrochemical Measurements

Electrochemical performances were evaluated based on 2032‑type coin cells. The sulfur composite, super P, and LA132 were dispersed in deionized water with stirring. The as‑obtained slurry was uniformly spread on the surface of carbon‑coated Al foil. After vacuum‑dried at 60 °C over‑night, the cathode plate was obtained. The sulfur loading of cathode is ca. 1.5 mg cm−2 if no special introduction. The assembly process of cells was conducted in Ar‑filled glove box with the sulfur cathode, lithium foil, separator, and liq‑uid electrolyte. The electrolyte is composed of 1 M lithium bis(trifluoromethane)sulfonimide (LiTFSI) in a mixture of

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1,3‑dioxolane/1,2‑dimethoxyethane (DOL/DME, v/v, 1:1) with the additive of 2 wt% LiNO3. Solartron 1400 electro‑chemical workstation was employed to obtain CV curves and electrochemical impedance spectroscopy (EIS) spectra. The measurement of CV curves was taken at the scanning rate of 0.1 mV s−1 with the voltage window of 1.8–2.8 V. Gal‑vanostatic charge/discharge was conducted by the LAND‑CT2001 instrument at various C‑rates (1 C = 1672 mA g−1) with potential range from 1.8 to 2.8 V.

3 Results and Discussion

Figure 1 illustrates the synthesis process of N‑Ti3C2 MXene, N‑Ti3C2@CNTs, and N‑Ti3C2@CNT microspheres. Firstly, Ti3C2 MXene nanosheets were obtained after etching of hydro‑fluoric acid and further sonication exfoliation. Ni2+ and HCl‑treated melamine (HTM) were selected as the catalyst precur‑sor and carbon source, respectively, which can be effectively adsorbed on the surface of negatively charged MXene sheets via the electrostatic force [29, 30]. As displayed in Fig. S1, uniform dark green solution indicates successful delamination of multilayered Ti3C2. When positively charged Ni2+ and/or HTM suspension were mixed with above solution, the obvious

precipitates and a clear supernatant can be observed. The pro‑cess is involved with electrostatic interaction between MXene sheets and Ni2+/HTM. Finally, porous N‑Ti3C2@CNT micro‑spheres are synthesized through the spray drying and pyroly‑sis. During the pyrolysis, Ni2+ was reduced to Ni to achieve the in situ growth of CNTs on the surface of MXene. Mean‑while, N‑rich HTM was decomposed to introduce N‑doping in the CNTs and Ti3C2. As comparison, N‑Ti3C2 MXene and N‑Ti3C2@CNTs were prepared by the route of Fig. 1.

Figure S10 shows XRD patterns of multilayered Ti3C2 and Ti3C2 nanosheets. After sonication exfoliation, the (0002) diffraction peak of Ti3C2 shifts to 6.3° from 9.1° and the intensity increases, demonstrating effective exfoliation of multilayered Ti3C2 [31]. Compared with Ti3C2 sheets, the peak of N‑Ti3C2 MXene shifts by 0.2° to 6.1°, which indi‑cates the existence of N‑doping in MXene structure [30, 32]. N‑dopants increase interlayer spacing of MXene layers due to larger atomic radius of nitrogen than carbon element, leading to slight shift of peak. The peaks located at 36.2°, 42.4°, and 61.5° belong to Ti3C2 MXene and no peaks of anatase or rutile type TiO2 can be observed, demonstrat‑ing good stability of MXene in the synthesis process [33]. For N‑Ti3C2@CNTs and N‑Ti3C2@CNT microspheres, the

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Fig. 1 Schematic illustration of preparation of a N‑Ti3C2, b N‑Ti3C2@CNTs, and c N‑Ti3C2@CNT microspheres

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additional peaks can be attributed to (002) plane of graphitic carbon (26.3°) and nickel (44.4° and 51.8°), respectively [34]. The results demonstrate successful synthesis of CNTs with the catalysis of Ni species. The XRD patterns (Fig. S14) of sulfur composites verify successful infiltration of orthorhombic sulfur by the simple melting diffusion strat‑egy. TGA was performed to evaluate sulfur proportion of sulfur composites. As shown in Fig. S15, the obvious mass loss from 180 to 350 °C was resulted from evaporation of sulfur under N2 atmosphere [35]. The sulfur content can be calculated as 71.6, 71.7, and 71.8% in N‑Ti3C2/S, N‑Ti3C2@CNTs/S, and N‑Ti3C2@CNT microspheres/S, respectively.

SEM and TEM were conducted to identify the morphol‑ogy and structure of as‑obtained materials. Multilayered Ti3C2 MXene (Fig. 2a, b) shows typical accordion‑like structure, demonstrating successful removal of Al layers. After sonication, MXene possesses nanosheet‑like mor‑phology with lateral sizes of several micrometers (Fig. 2c, d). Crumpled surface reveals good flexibility and ultrathin thickness, indicating successful preparation of high‑quality MXene nanosheets. TEM images (Fig. S2) show transparent flake‑like structure for Ti3C2 MXene nanosheets, indicat‑ing good exfoliation effect. N‑Ti3C2 (Fig. 2e) still maintains micro‑sized sheet‑like structure with distinct macropores on

Fig. 2 SEM images of a, b multilayered Ti3C2 MXene after etching, c, d Ti3C2 MXene nanosheets after exfoliation, e N‑Ti3C2, f, g N‑Ti3C2@CNTs, and h, i N‑Ti3C2@CNT microspheres

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the surface. TEM images (Fig. S3) obviously reveal nano‑sized micropores and mesopores in the N‑Ti3C2, which can be attributed to high temperature and reduction atmosphere produced by decomposition of melamine [36, 37]. The hierarchical pores are favorable to promote specific sur‑face area and pore volume. As shown in Fig. S5, the pre‑cursors are composed of porous microspheres after spray

drying. After pyrolysis, N‑Ti3C2@CNT microspheres still retain uniform sphere‑like morphology with particle size of 2–5 μm (Fig. 2h, i). TEM images (Fig. 3a–c) obviously reveal that N‑Ti3C2@CNT microsphere consists of inter‑connected CNTs and MXene nanosheets. In addition, some Ni nanoparticles are homogenously distributed within the microsphere. The small amount of Ni particles can not only

Fig. 3 a–c TEM and HRTEM images of N‑Ti3C2@CNT microspheres and d EDS elemental mapping of N‑Ti3C2@CNT microspheres/S com‑posite

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improve electronic conductivity, but also provide chemical confinement for polysulfides [38]. CNTs show bamboo‑like structure with fringes spacing of 0.35 nm corresponding to (002) planes [39], illustrating high graphitization degree of CNTs with the catalysis of Ni. EDS mapping (Fig. S6) testifies homogenous distribution of CNTs and MXene in the porous microsphere. For N‑Ti3C2@CNTs, CNTs are successfully synthesized and uniformly distributed on the surface of MXene to form interwoven porous morphology (Figs. 2f, g and S4).

After sulfur encapsulation, N‑Ti3C2@CNTs and N‑Ti3C2@CNT microspheres (Fig. S7c–f) still maintain previous structure and no distinct sulfur aggregation can be seen, indicating successful infiltration of sulfur into poros‑ity of microspheres. However, N‑Ti3C2 and sulfur aggre‑gate together to form clusters (Fig. S7a, b). And EDS map‑ping (Fig. S8) reveals that sulfur aggregation exists in the clusters. The result demonstrates the structure advantage of N‑Ti3C2@CNTs and N‑Ti3C2@CNT microspheres in accommodating sulfur compared with N‑Ti3C2 nanosheets. As displayed in Fig. 3d, sulfur has similar intensity within N‑Ti3C2@CNT microsphere, indicating uniform distribu‑tion of sulfur. Furthermore, elements of Ti, C, N, and Ni also homogenously dispersed in the region, which furtherly confirm that CNTs and MXene are uniformly distributed in the microsphere.

N2 adsorption/desorption measurement was taken to evaluate porous structure of materials. Ti3C2 nanosheets have higher specific surface area (SSA) and pore volume (PV) than that of multilayered Ti3C2 (Fig. S11), demon‑strating effective exfoliation. After pyrolysis with HTM, SSA, and PV of MXene (N‑Ti3C2) significantly increased to 263.3 m2 g−1 and 0.43 cm3 g−1 (Fig. S12), respectively. The isotherm curves of N‑Ti3C2@CNTs and N‑Ti3C2@CNT microspheres (Figs. S13 and 4b) exhibit typical IV‑type behavior with obvious hysteresis loop, which can be attributed to the existence of mesopores and macropo‑res [40]. In addition, the presence of micropores is evi‑denced by the rapid increase in N2 absorption when the relative pressure is close to zero [41]. N‑Ti3C2@CNTs and N‑Ti3C2@CNT microspheres possess high SSA of 358.4, 388.6 m2 g−1 and PV of 0.66, 0.72 cm3 g−1, respectively, which are much higher than that of N‑Ti3C2. The increased part can be assigned to the incorporation of MXene flakes and CNTs. The abundant porosity not only allows infiltra‑tion of enough sulfur, but also effectively buffers volume

expansion of electrodes. In addition, porous structure is favorable to electron/ion transformation and permeation of liquid electrolytes [42].

X‑ray photoelectron spectroscopy (XPS) was per‑formed to analyze elements content and condition. Fig‑ure 4c reveals the existence of C, Ti, N, and O elements in three kinds of materials. Especially, the peak of Ni can be observed in N‑Ti3C2@CNTs and N‑Ti3C2@CNT micro‑spheres, which catalyze in situ growth of CNTs. The Ti 2p spectra can be identified to three peaks located at 455.5, 456.9, and 458.5 eV (Fig. 4e), which corresponds to Ti–C, Ti–N, and Ti–O, respectively. The appearance of Ti–N bonding demonstrates N‑doping in Ti3C2 structure. The N‑Ti bonding in N 1s spectra (Fig. 4f) also verifies the existence of nitrogen dopants [32]. In addition to N–Ti peak, another three peaks centered at 397.4, 399.1, and 401.0 eV can be assigned to pyridinic N, pyrrolic N, and graphitic N [43, 44]. Pyridinic N is dominated among three kinds of N element, which is considered to be main immobilization sites of LiPSs for N‑doped materials [45]. Compared with N‑Ti3C2, the decrease in N‑Ti in N‑Ti3C2@CNTs can be ascribed to the presence of N‑doping in CNTs structure. High‑resolution C 1s spectra (Fig. 4d) consist of C–Ti, C=C, C–O, and C–N bodings. It can be noted that the peak intensity of C–N of N‑Ti3C2@CNTs and N‑Ti3C2@CNT microspheres is significantly higher than that of N‑Ti3C2, which reconfirms the existence of N‑doped CNTs. N‑doping exists in both of MXene and CNTs according to above results. The nitrogen content of N‑Ti3C2 MXene, N‑Ti3C2@CNTs, and N‑Ti3C2@CNT microspheres is up to 16.48, 10.98, and 11.86 at% (Table S2). The efficient N‑doping can not only promote electronic conductivity, but also improve the immobiliza‑tion ability for LiPSs [29, 34].

The CV curves of three sulfur cathodes (Figs. 5a and S16) exist two well‑defined cathodic peaks and one sharp anodic peak. The former peaks correspond to the reduc‑tion process from sulfur to long‑chain lithium polysulfides (LiPSs) and furtherly to Li2S2 and Li2S. The latter peak is associated with reversed transformation of above process [46–48]. It can be noted that the second reduction peak of N‑Ti3C2@CNT microspheres/S cathode is higher than that of N‑Ti3C2@CNTs/S and significantly higher than N‑Ti3C2/S cathode (Fig. 5b). The result demonstrates that N‑Ti3C2@CNT microspheres exhibit more favorable structure in facili‑tating electron/ion transformation [49]. The galvanostatic

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charge/discharge curves of N‑Ti3C2@CNTs/S (Fig. S17b) and N‑Ti3C2@CNT microspheres/S (Fig. 5d) cathodes show obvious discharge/charge plateaus even at high C‑rate of 4 C (1 C = 1672 mA g−1). However, the plateaus for N‑Ti3C2/S nearly disappear at high current density (Fig. S17a). The

difference can be attributed to the incorporation of CNTs into MXene, which effectively improves electronic conduc‑tivity leading to faster electrochemical kinetics. Figure 5c shows the rate capability. N‑Ti3C2@CNT microspheres/S cathode delivers reversible specific capacity of 1339.2,

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1093.3, 969.4, 856.3, 789.3, and 640.5 mAh g−1 at C‑rate of 0.1, 0.2, 0.5, 1, 2, and 4 C, respectively. High specific capacity of 1103.2 mAh g−1 can be retained when C‑rate decreases to 0.1 C, demonstrating excellent rate capabil‑ity [50]. The capacity performance is better than that of N‑Ti3C2@CNTs/S cathode and much better than N‑Ti3C2/S cathode.

The cycling performances at 0.2 C were investi‑gated and are displayed in Fig.  5e. N‑Ti3C2@CNT microspheres/S cathode exists initial capacity of 1124.6 mAh g−1 and reversible capacity of 1025.3 mAh g−1 after 200 cycles corresponding to high capacity retention (CR) up to 91.2%, which is significantly higher than that of N‑Ti3C2/S cathode (598.5 mAh g−1 after 200 cycles, CR 63.6%). N‑Ti3C2@CNTs/S cathode also shows good cycling stability with capacity of 835.9 mAh g−1 after 200 cycles and CR of 74.7%. The difference of cycling stability becomes more distinct at 1 C (Fig. 5f). The specific capac‑ity of N‑Ti3C2/S cathode decreases to only 358.5 mAh g−1 after 400 cycles with low cycling stability. N‑Ti3C2@CNTs/S cathode exhibits specific capacity of 874.9 mAh g−1 and maintains capacity of 604.5 mAh g−1 after 700 cycles with low capacity fading rate (FR) of 0.044% per cycle. N‑Ti3C2@CNT microspheres/S cathode shows highly stable cycling performance up to 1000 cycles. Particularly, the cathode delivers initial capacity of 927.5 mAh g−1 and reversible capacity of 775.6 mAh g−1 after 1000 cycles with extremely low FR of only 0.016% per cycle. Good cycling stability is remarkable compared with reported studies (Table S3). EIS was investigated to clarify improved electrochemical performance. The plots show one depressed semicircle and a sloped line before cycling (Fig. 6c), which correspond to charge transfer resistance (Rct) and charge diffusion resistance (W), respectively [51]. Rct orderly diminishes from N‑Ti3C2/S and N‑Ti3C2@CNTs/S to N‑Ti3C2@CNT microspheres/S cathode, which reveals enhanced conductivity of relevant host materials. Additional semicircle emerges at high‑frequency region after cycling (Fig. 6d), which is associated with the resist‑ance of insulating Li2S layers (Rg) derived from uncon‑verted part during charge [52]. Rg and Rct of N‑Ti3C2@CNT microspheres/S are lower than that of N‑Ti3C2/S and N‑Ti3C2@CNTs/S, demonstrating an efficient redox pro‑cess of electrode.

Cycling performance at high C‑rate and high sulfur loading was tested and is shown in Fig. 6e, f, respectively.

N‑Ti3C2@CNT microspheres/S cathode exhibits high capac‑ity of 788.6 mAh g−1 and retains reversible capacity of 647.6 mAh g−1 after 650 cycles at high C‑rate of 4 C with low fading rate of 0.027% per cycle, indicating excellent cycle stability. At high sulfur loading of 3 mg cm−2, a specific capacity of 665 mAh g−1 after 800 cycles with low fading rate of 0.039% per cycle can be achieved. As sulfur loading increasing to 6 mg cm−2, N‑Ti3C2@CNT microspheres/S cathode still shows highly stable cycling with low decay rate of 0.051% per cycle. Excellent cycling stability can be ascribed to strong immobilization for LiPSs originating from polar surface of MXene and effective N‑doping in Ti3C2 and CNTs.

The adsorption measurement of LiPSs was taken to com‑pare anchoring ability of several host materials (Fig. S22). After standing for only 15 min, the color of containing N‑Ti3C2, N‑Ti3C2@CNTs, or N‑Ti3C2@CNT microspheres becomes shallow compared with the pristine Li2S6 solution, implying efficient adsorption for LiPSs [53]. However, there is no obvious change for the solution containing CNTs. The difference indicates that polar Ti3C2 can provide stronger confinement for LiPSs than CNTs. Finally, N‑Ti3C2@CNT microspheres show the best adsorption effect for LiPSs, which can be attributed to porous structure with higher spe‑cific surface area to provide more adsorption sites for LiPSs. We also disassembled cells before and after cycling to evalu‑ate change of electrodes. As shown in Fig. S19, the surface of N‑Ti3C2/S cathode was almost covered by a passivation layer after cycling [54, 55]. In contrast, the host materials still maintain pristine morphology even though some pas‑sivation layer can be observed for N‑Ti3C2@CNTs/S and N‑Ti3C2@CNT microspheres/S electrodes (Figs. S20, S21). The result is consistent with above discussion. N‑Ti3C2@CNT microspheres not only provide strong immobilization for LiPSs, but also maintain morphology stability during cycling due to highly interwoven structure of MXene and CNTs. In addition, Fig. 6a, b shows the Ti 2p and S 2p spectra of N‑Ti3C2@CNT microspheres/Li2S6. Compared with pristine N‑Ti3C2@CNT microspheres, there is the typical peak of Ti–S bonding located at 456.1 eV, which can be ascribed to Lewis acid–base interaction originating from polar surface of MXene and polysulfide species [53, 56]. High‑resolution S 2p spectra can be deconvoluted to thiosulfate (168.0 eV) and polythionate (169.5 eV) com‑plexes, together with remained polysulfides (ST 160.9 eV, SB 162.4 eV) [25]. The thiosulfate/polythionate species are

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1st2nd3rd4th5th

(a)

(c)

(e)

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(b)0.0020

0.0015

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0.0005

0.0000

−0.0005

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0.1C

0.2C0.5C

1C2C 4C

0.1C

Voltage (V vs. Li/Li+)2.4 2.6 2.8 1.90 2.00 2.05

4C, 2C, 1C, 0.5C, 0.2C, 0.1C

2.0 2.2 2.10 2.202.151.95

N-Ti3C2@CNTs microspheres/S

N-Ti3C2@CNTs microspheres/S

N-Ti3C2/SN-Ti3C2@CNTs/SN-Ti3C2@CNTs microspheres/S

N-Ti3C2/SN-Ti3C2@CNTs/SN-Ti3C2@CNTs microspheres/S

N-Ti3C2/SN-Ti3C2@CNTs/SN-Ti3C2@CNTs microspheres/S

2.062 V

2.065 V2.070 V

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(mAh

g−1

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Volta

ge (V

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effic

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y (%

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Voltage (V)

Fig. 5 a CV curve of N‑Ti3C2@CNT microspheres/S cathode at the scanning rate of 0.1 mV s−1. b Magnification of cathodic peaks (voltage range of 1.9–2.2 V). c Rate capability of three cathodes at different C‑rate (the calculation of specific capacity is based on the weight of sulfur in the cathode). d The gal‑vanostatic charge/discharge curves for N‑Ti3C2@CNT microspheres/S cathode at various C‑rates. Cycling performance of three cathodes at e 0.2 C and f 1 C

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N-Ti3C2/SN-Ti3C2@CNTs/SN-Ti3C2@CNTs microspheres/S

N-Ti3C2@CNTs microspheres/S cathode at 4CSpe

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Ti-S

Ti-N

Ti-O

158 160 162 164 166 168 170 172

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nsity

(a.u

.)

Binding energy (eV)

S 2p(b) STSBThiosulfatePolythionate

−Z" (

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0 100 200 300 400 500 600 700 800Cycle number

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Fig. 6 a Ti 2p and b S 2p spectra of N‑Ti3C2@CNT microspheres/Li2S6. EIS spectra of sulfur cathodes c before and d after cycles. Cycling per‑formance of N‑Ti3C2@CNT microspheres/S cathode at e high C‑rate of 4 C and f high sulfur loading

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derived from exposed Ti and hydroxyl groups on the surface of MXene [57].

On the basis of above discussion, excellent electrochemi‑cal performance of N‑Ti3C2@CNT microspheres/S cathode can be attributed to the following merits: (1) high specific surface area and pore volume can ensure uniform distribu‑tion of sulfur in the microspheres and effectively buffer volume expansion of electrodes during discharging; (2) MXene nanosheets interact with CNTs within the micro‑sphere to construct conductive and porous structure, which improves electrochemical reaction kinetics of electrodes; (3) Ti3C2 MXene exists Lewis acidic affinity with LiPSs, which effectively relieves shuttle effect resulting in highly stable cycling performance. Especially, porous structure and high N‑doping can further promote confinement ability of LiPSs.

4 Conclusion

In conclusion, we successfully synthesized porous N‑Ti3C2@CNT microspheres through a facile strategy with low‑cost materials (NiCl2 and HCl‑treated melamine). Melamine, as the source of carbon and nitrogen, not only realizes in situ growth of N‑doped CNTs on the MXene nanosheets, but also provides efficient N‑doping in the Ti3C2 structure. Within the microspheres, MXene flakes connect with CNTs con‑structing highly conductive and porous network to accom‑modate active sulfur and effectively confine polysulfides. In addition, Ni nanoparticles homogenously distribute within the microspheres, which can furtherly promote conductivity of electrodes and tightly entrap LiPSs in the region of micro‑spheres. Above‑mentioned merits make N‑Ti3C2@CNTs microsphere an ideal sulfur host material. When employed as sulfur host in Li–S battery, N‑Ti3C2@CNT microsphere/S cathode shows high capacity performance, excellent rate capability, and long‑term cycling stability. Furthermore, superior cycling performance even at high C‑rate of 4 C and sulfur loading (3 and 6 mg cm−2) can be achieved. Last but not the least, the strategy can be extended to prepare other CNT microsphere composites and shows great potential in the field of energy storage.

Acknowledgements The authors acknowledge support by Taihu Electric Corporation.

Open Access This article is licensed under a Creative Commons Attribution 4.0 International License, which permits use, sharing,

adaptation, distribution and reproduction in any medium or format, as long as you give appropriate credit to the original author(s) and the source, provide a link to the Creative Commons licence, and indicate if changes were made. The images or other third party material in this article are included in the article’s Creative Com‑mons licence, unless indicated otherwise in a credit line to the material. If material is not included in the article’s Creative Com‑mons licence and your intended use is not permitted by statutory regulation or exceeds the permitted use, you will need to obtain permission directly from the copyright holder. To view a copy of this licence, visit http://creat iveco mmons .org/licen ses/by/4.0/.

Electronic supplementary material The online version of this article (https ://doi.org/10.1007/s4082 0‑019‑0341‑6) contains supplementary material, which is available to authorized users.

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